JPH11315327A - Manufacture of non-oriented silicon steel sheet with low iron loss, and non-oriented silicon steel sheet with low iron loss - Google Patents
Manufacture of non-oriented silicon steel sheet with low iron loss, and non-oriented silicon steel sheet with low iron lossInfo
- Publication number
- JPH11315327A JPH11315327A JP10134233A JP13423398A JPH11315327A JP H11315327 A JPH11315327 A JP H11315327A JP 10134233 A JP10134233 A JP 10134233A JP 13423398 A JP13423398 A JP 13423398A JP H11315327 A JPH11315327 A JP H11315327A
- Authority
- JP
- Japan
- Prior art keywords
- iron loss
- steel sheet
- less
- annealing
- low iron
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Landscapes
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、電気材料として用
いられるのに好適な、鉄損の低い無方向性電磁鋼板、及
びその製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a non-oriented electrical steel sheet having a low iron loss and suitable for use as an electrical material, and a method for producing the same.
【０００２】[0002]
【従来の技術】近年、電気機器の省エネルギーの観点よ
り、より鉄損の低い電磁鋼板が求められるようになって
いる。この鉄損を低減するためには結晶粒の粗大化が効
果的であり、低鉄損が特に要求されるSi+Al量が１〜３
％程度の中・高級グレードの無方向性電磁鋼板において
は、仕上焼鈍温度を1000℃程度まで高めたり、焼鈍時の
ラインスピードを下げ、焼鈍時間を長くすることにより
結晶粒の粗大化を図っている。2. Description of the Related Art In recent years, electromagnetic steel sheets having lower iron loss have been demanded from the viewpoint of energy saving of electric equipment. In order to reduce the iron loss, it is effective to increase the crystal grain size.
% Of medium- and high-grade non-oriented electrical steel sheets, increase the finish annealing temperature to about 1000 ° C, lower the line speed during annealing, and increase the annealing time to increase the grain size. I have.
【０００３】この仕上焼鈍時の粒成長性を良好にするた
めには、鋼板中の介在物、析出物量を低減することが効
果的である。このため、これまで介在物、析出物を無害
化することが試みられており、特に高級材ではMnＳの析
出防止の観点からＳ量を低減させる試みがなされてき
た。In order to improve the grain growth during the finish annealing, it is effective to reduce the amount of inclusions and precipitates in the steel sheet. For this reason, attempts have been made to render the inclusions and precipitates harmless, and particularly in high-grade materials, attempts have been made to reduce the S content from the viewpoint of preventing precipitation of MnS.
【０００４】例えば、特公昭５６−２２３９１号公報に
は、Si：2.5〜3.5％、Al：0.3〜1.0％の鋼においてＳを
50ppm以下、Ｏを25ppm以下とすることにより鉄損を低下
させる技術が開示されている。[0004] For example, Japanese Patent Publication No. 56-22391 discloses that S is contained in steel of 2.5 to 3.5% Si and 0.3 to 1.0% of Al.
A technique for reducing iron loss by setting the content of O to 50 ppm or less and the content of O to 25 ppm or less is disclosed.
【０００５】また、特公平２−５０１９０号公報には、
Si：2.5〜3.5％、Al：0.25〜1.0％の鋼においてＳを15p
pm以下、Ｏを20ppm以下、Ｎを25ppm以下とすることによ
り鉄損を低下させる技術が開示されている。In Japanese Patent Publication No. 2-50190,
Si: 2.5-3.5%, Al: 0.25-1.0% S in steel 15p
There is disclosed a technique for reducing iron loss by setting pm or less, O to 20 ppm or less, and N to 25 ppm or less.
【０００６】さらに特開平５−１４０６４７号公報に
は、Si：2.0〜4.0％、Al：0.10〜2.0％の鋼においてＳ
を30ppm以下、Ti、Zr、Nb、Ｖをそれぞれ50ppm以下とす
ることにより鉄損を低下させる技術が開示されている。Further, Japanese Patent Application Laid-Open No. Hei 5-140647 discloses that S: 2.0 to 4.0% and Al: 0.10 to 2.0%
A technique for reducing iron loss by reducing Ti to 30 ppm or less and Ti, Zr, Nb, and V to 50 ppm or less, respectively, is disclosed.
【０００７】[0007]
【発明が解決しようとする課題】しかし、これらいずれ
の技術においても、Si、Al量がトータルで３〜3.5％程
度、Ｓ含有量を10ppm以下とした高級グレードの鋼板の
鉄損値は、Ｗ15/50＝2.4Ｗ／kg程度（板厚0.5mm）であ
り、これ以上の低鉄損は達成されていないのが現状であ
る。However, in any of these techniques, the iron loss value of a high-grade steel sheet having a total Si and Al content of about 3 to 3.5% and an S content of 10 ppm or less is W 15/50 = about 2.4 W / kg (sheet thickness 0.5 mm), and no further low iron loss has been achieved at present.
【０００８】本発明はこのような問題点を解決するため
になされたものであり、仕上焼鈍後の鉄損のより低い無
方向性電磁鋼板を提供することを課題とする。[0008] The present invention has been made to solve such a problem, and an object of the present invention is to provide a non-oriented electrical steel sheet having lower iron loss after finish annealing.
【０００９】[0009]
【課題を解決するための手段】本発明の骨子は、Ｓ＝10
ppm以下の極低Ｓ材において、Ｐを0.03〜0.15％、ある
いはSb＋1/2Snを0.001〜0.05％の範囲で含有させ、か
つ、熱延時の巻取温度を制御することにより、無方向性
電磁鋼板の鉄損を大幅に低下させることにある。The gist of the present invention is that S = 10
Non-oriented electrical steel sheets by containing P in the range of 0.03 to 0.15% or Sb + 1 / 2Sn in the range of 0.001 to 0.05% and controlling the winding temperature during hot rolling in ultra-low S materials of less than ppm To significantly reduce iron loss.
【００１０】すなわち、前記課題は、重量％で、Ｃ：0.
005％以下、Si：1.5〜3.5％、Mn：0.05〜1.0％、Ｎ：0.
005％以下（０を含む）、Al：0.1 〜1.0％、Ｓ：0.001
％以下（０を含む）、Ｐ：0.03〜0.15％を含み、残部が
実質的にFeからなるスラブを巻取温度750℃以下で熱間
圧延し、引き続き熱延板焼鈍を行ない、酸洗後、一回の
冷間圧延、もしくは中間焼鈍をはさんだ二回以上の冷間
圧延により、所定の板厚とし、仕上焼鈍を実施すること
を特徴とする鉄損の低い無方向性電磁鋼板の製造方法
（請求項１）により解決される。[0010] That is, the above-mentioned problem is expressed by:
005% or less, Si: 1.5-3.5%, Mn: 0.05-1.0%, N: 0.
005% or less (including 0), Al: 0.1 to 1.0%, S: 0.001
% Or less (including 0), P: 0.03 to 0.15%, and the remainder substantially consisting of Fe is hot-rolled at a winding temperature of 750 ° C. or less, subsequently hot-rolled sheet annealing, and after pickling The production of non-oriented electrical steel sheets with low iron loss, characterized in that the steel sheet has a predetermined thickness and is subjected to finish annealing by one or more cold rolling steps or two or more cold rolling steps with intermediate annealing. It is solved by a method (claim 1).
【００１１】また、前記課題は、重量％で、Ｃ：0.005
％以下、Si：1.5〜3.5％、Mn：0.05〜1.0％、Ｎ：0.005
％以下（０を含む）、Al：0.1 〜1.0％、Ｓ：0.001％以
下（０を含む）、Ｐ：0.15％以下（０を含む）、Sb＋1/
2Sn：0.001〜0.05％を含み、残部が実質的にFeからなる
スラフ゛を巻取温度750℃以下で熱間圧延し、引き続き熱延
板焼鈍を行ない、酸洗後、一回の冷間圧延、もしくは中
間焼鈍をはさんだ二回以上の冷間圧延により、所定の板
厚とし、仕上焼鈍を実施することを特徴とする鉄損の低
い無方向性電磁鋼板の製造方法（請求項２）によっても
解決される。[0011] The above-mentioned problem is expressed as follows: C: 0.005% by weight.
% Or less, Si: 1.5 to 3.5%, Mn: 0.05 to 1.0%, N: 0.005
% Or less (including 0), Al: 0.1 to 1.0%, S: 0.001% or less (including 0), P: 0.15% or less (including 0), Sb + 1 /
2Sn: 0.001 to 0.05%, the remainder substantially consisting of Fe, hot rolled at a winding temperature of 750 ° C. or lower, subsequently hot-rolled sheet annealing, pickling, one cold rolling, Alternatively, according to a method for producing a non-oriented electrical steel sheet having a low iron loss, characterized in that a predetermined thickness is obtained by cold rolling two or more times with intermediate annealing and finish annealing is performed (claim 2). Will be resolved.
【００１２】さらに、前記課題は、前記第１の手段又は
第２の手段によって製造される鉄損の低い無方向性電磁
鋼板（請求項３）によっても解決される。Further, the above-mentioned object is also achieved by a non-oriented electrical steel sheet having a low iron loss manufactured by the first means or the second means.
【００１３】ここに、「残部が実質的にFeである」とは、
不可避不純物の他、本発明の作用効果を無くさない範囲
で他の微量元素を添加したものも、本発明の範囲に含ま
れる趣旨である。なお、以下の説明において、鋼の成分
を示す％は全て重量％であり、ppmも重量ppmである。Here, "the balance is substantially Fe" means:
In addition to the unavoidable impurities, those to which other trace elements are added within a range that does not impair the effects of the present invention are included in the scope of the present invention. In the following description, all the percentages indicating the components of steel are% by weight, and ppm is also ppm by weight.
【００１４】（発明に至る経緯）本発明者らは、Ｓ＝10
ppm以下の極低Ｓ材において鉄損低減を阻害している要
因を詳細に調査した。その結果、Ｓ量の低減に伴い、鋼
板表層部に顕著な窒化層が認められ、この窒化層が鉄損
低減を阻害している事が明らかとなった。そこで、本発
明者らが、窒化を抑制し、鉄損をさらに低減させる手法
に関し鋭意検討した結果、Ｐを0.03〜0.15％、あるいは
Sb＋1/2Snを0.001〜0.05％の範囲で含有させ、かつ、熱
延時の巻取温度を制御することにより、極低Ｓ材の鉄損
が大幅に低下することを見出した。(Circumstances leading to the invention) The present inventors have found that S = 10
Factors that hinder reduction of iron loss in extremely low S materials of less than ppm were investigated in detail. As a result, a remarkable nitrided layer was observed in the surface layer of the steel sheet as the S content was reduced, and it was clarified that the nitrided layer hindered the reduction of iron loss. Therefore, the present inventors have conducted intensive studies on a technique for suppressing nitriding and further reducing iron loss. As a result, P was set to 0.03 to 0.15% or
By containing Sb + 1 / 2Sn in the range of 0.001 to 0.05% and controlling the winding temperature during hot rolling, it has been found that the core loss of the extremely low S material is significantly reduced.
【００１５】本発明を実験結果に基づいて詳細に説明す
る。最初に、鉄損に及ぼすS量の影響を調査するため、
以下の３種の成分系についてＳ量をtr. 〜１５ppm の範
囲で変化させた鋼を実験室にて真空溶解し、製造された
スラブを1160℃で1hr加熱し、巻取温度の異なる３種類
の熱延板サンプルを作成した。この後、10％Ｈ2-90％Ｎ
2雰囲気中で900℃×90秒の熱延板焼鈍を施した後、酸洗
を施し、その後、板厚0.5mmまで冷間圧延し、10％Ｈ2-9
0％Ｎ2雰囲気で930℃×2min間の仕上焼鈍を行った。 Ｃ：0.0025％、Si：1.85％、Mn：0.20％、Ｐ：0.040
％、Al：0.31％、Ｎ：0.0018％、 Ｃ：0.0025％、Si：1.85％、Mn：0.20％、Ｐ：0.010
％、Al：0.31％、Ｎ：0.0018％、Sn：0.0050％ Ｃ：0.0025％、Si：1.85％、Mn：0.20％、Ｐ：0.010
％、Al：0.31％、Ｎ：0.0018％、Sb：0.0040％The present invention will be described in detail based on experimental results. First, to investigate the effect of S content on iron loss,
In the laboratory, steel with the S content varied from tr. To 15 ppm in the following three component systems was vacuum-melted, and the manufactured slab was heated at 1160 ° C for 1 hour, and three types with different winding temperatures were used. A hot rolled sheet sample was prepared. After this, 10% H 2 -90% N
(2 ) After subjecting a hot-rolled sheet to annealing at 900 ° C. for 90 seconds in an atmosphere, pickling is performed, and then cold-rolled to a sheet thickness of 0.5 mm, and 10% H 2 -9
Finish annealing was performed at 930 ° C. for 2 minutes in a 0% N 2 atmosphere. C: 0.0025%, Si: 1.85%, Mn: 0.20%, P: 0.040
%, Al: 0.31%, N: 0.0018%, C: 0.0025%, Si: 1.85%, Mn: 0.20%, P: 0.010
%, Al: 0.31%, N: 0.0018%, Sn: 0.0050% C: 0.0025%, Si: 1.85%, Mn: 0.20%, P: 0.010
%, Al: 0.31%, N: 0.0018%, Sb: 0.0040%
【００１６】図１にこのようにして得られたサンプルの
Ｓ量と鉄損Ｗ15/50の関係を示す。図１より、Ｓ≦10ppm
となった場合に大幅に鉄損が低減され、Ｗ15/50＝2.5
Ｗ／kgが達成されることがわかる。これはＳ量低減によ
り粒成長性が大幅に向上したためである。以上のことよ
り本発明に於いては、Ｓ量の範囲を10ppm以下、望まし
くは5ppm以下に限定する。FIG. 1 shows the relationship between the S content of the sample thus obtained and the iron loss W 15/50 . From FIG. 1, S ≦ 10 ppm
, Iron loss is greatly reduced, W 15/50 = 2.5
It can be seen that W / kg is achieved. This is because grain growth was greatly improved by reducing the amount of S. From the above, in the present invention, the range of the amount of S is limited to 10 ppm or less, preferably 5 ppm or less.
【００１７】しかし、Ｓ量が10ppm以下での鉄損の低下
レベルは、熱延時の巻取温度によって異なる事がわかっ
た。すなわち、図１を見ると明らかなように、巻取温度
が650℃及び720℃の場合には、800℃の場合に比して、
鉄損が大きく低下している。However, it has been found that the level of reduction in iron loss when the S content is 10 ppm or less depends on the winding temperature during hot rolling. That is, as is apparent from FIG. 1, when the winding temperature is 650 ° C. and 720 ° C., as compared with the case where the winding temperature is 800 ° C.,
Iron loss has dropped significantly.
【００１８】本発明者らは、この原因を調査するため、
光学顕微鏡にて組織観察を行った。その結果、800℃巻
取の場合には、鋼板表層に顕著な窒化層が認められた。
これに対し、650℃巻取、720℃巻取の場合には窒化層は
軽微となっていた。この窒化層は、熱延巻取時のスケー
ル生成量の差に依存するものと推定され、800℃巻取の
場合の窒化層は、窒化雰囲気で行なった熱延板焼鈍時
に、スケールが触媒となって生じたものと考えられる。The present inventors investigated the cause of this,
The structure was observed with an optical microscope. As a result, in the case of winding at 800 ° C., a remarkable nitride layer was recognized on the surface layer of the steel sheet.
On the other hand, in the case of 650 ° C. winding and 720 ° C. winding, the nitrided layer was slight. It is presumed that this nitrided layer depends on the difference in the amount of scale generated during hot rolling and the nitrided layer in the case of 800 ° C winding is such that when the hot rolled sheet is annealed in a nitriding atmosphere, the scale reacts with the catalyst. It is considered that this occurred.
【００１９】Ｓ量により窒化反応が異なった原因に関し
ては次のように考えられる。すなわち、Ｓは表面および
粒界に濃化しやすい元素であることから、Ｓ＞10ppm の
領域では、Ｓが鋼板表面へ濃化し、熱延板焼鈍時の窒素
の吸着を抑制した。一方、Ｓ≦10ppm の領域ではＳによ
る窒素吸着の抑制効果が低下した。これを、Ｐあるいは
Sn、あるいはSbの添加量により補おうとしたが、熱延時
の巻取温度によって、窒素吸着抑制能力に差があり、こ
れが鉄損レベルに反映された。The reason why the nitridation reaction differs depending on the amount of S is considered as follows. That is, since S is an element that easily concentrates on the surface and grain boundaries, in the region of S> 10 ppm, S concentrates on the steel sheet surface, and suppresses the adsorption of nitrogen during annealing of the hot-rolled sheet. On the other hand, in the range of S ≦ 10 ppm, the effect of suppressing the adsorption of nitrogen by S was reduced. This is P or
An attempt was made to compensate for the addition amount of Sn or Sb, but there was a difference in the ability to suppress nitrogen adsorption depending on the winding temperature during hot rolling, and this was reflected in the iron loss level.
【００２０】次に熱延時の最適巻取温度範囲を調査する
ため、以下の３種の成分系の鋼を実験室にて真空溶解し
て製造したスラブを1160℃で１hr加熱後、巻取温度の異
なる熱延板を種々作成した。 Ｃ：0.0020％、Si：1.87％、Mn：0.20％、Ｐ：0.040
％、Al：0.30％、Ｓ：0.0003％、Ｎ：0.0017％ Ｃ：0.0020％、Si：1.87％、Mn：0.20％、Ｐ：0.010
％、Al：0.30％、Ｓ：0.0003％、Ｎ：0.0017％、Sn：0.
0050％ Ｃ：0.0020％、Si：1.87％、Mn：0.20％、Ｐ：0.010
％、Al：0.30％、Ｓ：0.0003％、Ｎ：0.0017％、Sb：0.
0040％Next, in order to investigate the optimum winding temperature range during hot rolling, a slab produced by vacuum melting of the following three types of steels in a laboratory was heated at 1160 ° C. for 1 hour, and then the winding temperature was increased. Various hot rolled sheets of different types were prepared. C: 0.0020%, Si: 1.87%, Mn: 0.20%, P: 0.040
%, Al: 0.30%, S: 0.0003%, N: 0.0017% C: 0.0020%, Si: 1.87%, Mn: 0.20%, P: 0.010
%, Al: 0.30%, S: 0.0003%, N: 0.0017%, Sn: 0.
0050% C: 0.0020%, Si: 1.87%, Mn: 0.20%, P: 0.010
%, Al: 0.30%, S: 0.0003%, N: 0.0017%, Sb: 0.
0040%
【００２１】この後、10％Ｈ2-90％Ｎ2雰囲気中で900℃
×90秒の熱延板焼鈍、酸洗を施し、その後、板厚0.5mm
まで冷間圧延し、10％Ｈ2-90％Ｎ2雰囲気で930℃×２mi
n間の仕上焼鈍を行った。図２はこのようにして得られ
たサンプルの熱延時巻取温度と鉄損Ｗ15/50の関係を示
したものである。図２より、何れの成分系についても、
熱延時の巻取温度750℃以下で鉄損が低下し、Ｗ15/50＝
2.5Ｗ／kgが達成されることがわかる。Thereafter, 900 ° C. in a 10% H 2 -90% N 2 atmosphere.
Apply hot rolled sheet annealing and pickling for 90 seconds, then 0.5 mm thick
Cold rolled to 930 ° C x 2mi in an atmosphere of 10% H 2 -90% N 2
Finish annealing between n was performed. FIG. 2 shows the relationship between the coiling temperature during hot rolling and the iron loss W15 / 50 of the sample thus obtained. From FIG. 2, for each component system,
Iron loss decreases at a winding temperature of 750 ° C or less during hot rolling, and W 15/50 =
It can be seen that 2.5 W / kg is achieved.
【００２２】（その他の成分の限定理由）次に、その他
の成分の限定理由について説明する。 Ｃ： Ｃは磁気時効の問題があるため0.005％以下とす
る。 Ｎ： Ｎは、含有量が多い場合にはAlNの析出量が多く
なり、鉄損を増大させるため0.005％以下とする。 Si： Siは鋼板の固有抵抗を上げるために有効な元素で
あり、このため下限を1.5％とする。一方、3.5％を超え
ると飽和磁束密度の低下に伴い磁束密度が低下するため
上限を3.5％とする。 Mn： Mnは熱間圧延時の赤熱脆性を防止するために、0.
05％以上必要であるが、1.0％以上になると磁束密度を
低下させるので0.05〜1.0％とする。 Al： AlはSiと同様、固有抵抗を上げるために有効な元
素であるが、1.0％を超えると飽和磁束密度の低下に伴
い磁束密度が低下するため上限を1.0％とする。また、
0.1％未満の場合にはAlＮが微細化し粒成長性が低下す
るため下限を0.1％とする。(Reasons for Limiting Other Components) Next, reasons for limiting other components will be described. C: C is 0.005% or less because of the problem of magnetic aging. N: N is set to 0.005% or less to increase the amount of AlN and increase iron loss when the content is large. Si: Si is an element effective for increasing the specific resistance of the steel sheet, and therefore, the lower limit is set to 1.5%. On the other hand, if it exceeds 3.5%, the magnetic flux density decreases as the saturation magnetic flux density decreases, so the upper limit is set to 3.5%. Mn: Mn is 0.1% to prevent red hot brittleness during hot rolling.
It is required to be not less than 05%, but if it is not less than 1.0%, the magnetic flux density is reduced. Al: Al is an element effective for increasing the specific resistance, like Si, but if it exceeds 1.0%, the magnetic flux density decreases with a decrease in the saturation magnetic flux density, so the upper limit is set to 1.0%. Also,
If it is less than 0.1%, the lower limit is set to 0.1% because AlN becomes finer and the grain growth is reduced.
【００２３】Ｐ： Ｐは熱延板焼鈍時および仕上焼鈍時
の窒素の吸着を抑制するために、0.03％以上とし、冷間
圧延性の問題から上限を0.15％とする。ただし、Sb＋1/
2Snが0.001％以上含まれるときは、Sb、Snが熱延板焼鈍
時および仕上焼鈍時の窒素の吸着を抑制するので、下限
は設けず（０の場合でもよい）、冷間圧延性の問題から
上限を0.15％とする。 Sb＋1/2Sn：熱延板焼鈍時および仕上焼鈍時の窒化を軽
減するために有効な元素であり、同一の働きをするが、
Snの効果は、Sbに比して1/2である。よって、含有量をS
b＋1/2Snで規定する。熱延板焼鈍時および仕上焼鈍時の
窒素の吸着を抑制するためには、Sb＋1/2Snは0.001％以
上含有させることが好ましいが、コストの点から上限を
500ppmとする。なお、Sb+1/2Snがこの範囲であれば、一
方のみを含んでいてもよい。P: P is set to 0.03% or more in order to suppress nitrogen adsorption during hot-rolled sheet annealing and finish annealing, and the upper limit is set to 0.15% due to the problem of cold rolling. However, Sb + 1 /
When 2Sn is contained at 0.001% or more, since Sb and Sn suppress the adsorption of nitrogen during hot-rolled sheet annealing and finish annealing, there is no lower limit (0 may be used), and there is a problem of cold rolling property. From 0.15%. Sb + 1 / 2Sn: An element effective to reduce nitriding during hot-rolled sheet annealing and finish annealing, and has the same function.
The effect of Sn is 1/2 that of Sb. Therefore, the content is S
Specified by b + 1 / 2Sn. In order to suppress the adsorption of nitrogen during hot-rolled sheet annealing and finish annealing, it is preferable that Sb + 1 / 2Sn be contained at 0.001% or more.
500 ppm. If Sb + 1 / 2Sn is within this range, only one of them may be included.
【００２４】（製造方法）本発明においては、転炉で吹
練した溶鋼を脱ガス処理して所定の成分に調整し、引き
続き鋳造、熱間圧延を行う。熱間圧延時の仕上焼鈍温度
は特に規定する必要はなく、通常の無方向性電磁鋼板を
製造する範囲の温度でかまわない。熱延板焼鈍後、酸洗
を行い、次いで一回の冷間圧延、もしくは中間焼鈍をは
さんだ２回以上の冷間圧延により所定の板厚とした後
に、最終焼鈍を行う。(Manufacturing method) In the present invention, molten steel blown in a converter is degassed to adjust to a predetermined component, followed by casting and hot rolling. The finish annealing temperature at the time of hot rolling does not need to be particularly specified, and may be a temperature in a range where a normal non-oriented electrical steel sheet is manufactured. After the hot-rolled sheet annealing, pickling is performed, and then a single sheet of cold rolling or two or more cold-rolling steps including intermediate annealing is performed to obtain a predetermined sheet thickness, and then final annealing is performed.
【００２５】[0025]
【実施例】表1に示す鋼を用い、転炉で吹練した後に脱
ガス処理を行うことにより所定の成分に調整後鋳造し、
スラブ加熱温度1160℃で１hr加熱した後、板厚2.0 mmま
で熱間圧延を行った。熱間圧延時の仕上温度、巻取温度
およびその後の熱延板焼鈍条件は表１に示す内容で行な
った。酸洗後、板厚0.5mmまで冷間圧延を行い、表１に
示す仕上焼鈍条件で焼鈍を行った。磁気測定は25cmエプ
スタイン試験片を用いて行った。各鋼板の磁気特性を表
１に併せて示す。EXAMPLES Using the steel shown in Table 1, after degassing by blowing in a converter, the steel was adjusted to predetermined components and cast.
After heating at a slab heating temperature of 1160 ° C. for 1 hour, hot rolling was performed to a sheet thickness of 2.0 mm. The finishing temperature, winding temperature, and subsequent hot rolled sheet annealing conditions during hot rolling were as shown in Table 1. After pickling, cold rolling was performed to a sheet thickness of 0.5 mm, and annealing was performed under finish annealing conditions shown in Table 1. Magnetic measurements were performed using 25 cm Epstein specimens. Table 1 also shows the magnetic properties of each steel sheet.
【００２６】表１において、No.１〜No.16の鋼板はSiの
レベルが1.8％のオーダにあり、No.17〜No.23の鋼板はS
iのレベルが2.5％のオーダにある。同じSiのレベル同士
で比較した場合、本発明鋼の方が、鉄損Ｗ15/50が低
い。In Table 1, the steel sheets No. 1 to No. 16 have an Si level on the order of 1.8%, and the steel sheets No. 17 to No.
The level of i is on the order of 2.5%. When compared at the same Si level, the steel of the present invention has lower iron loss W15 / 50 .
【００２７】これより、鋼板成分のＳ量、P、Sn、Sb何
れか1種の添加量、および熱延時の巻取温度の何れもを
本発明の範囲とした場合に、鉄損の非常に低い無方向性
電磁鋼板が得られることがわかる。Thus, when the S content of the steel sheet component, the addition amount of any one of P, Sn, and Sb, and the winding temperature during hot rolling were all within the ranges of the present invention, the iron loss was extremely low. It is understood that a low non-oriented electrical steel sheet can be obtained.
【００２８】これに対して、No.9とNo.21の鋼板は、Ｓ
が本発明の範囲を外れているため、鉄損Ｗ15/50が高く
なっている。また、No.15とNo.22の鋼板は、熱延時の巻
取温度が本発明の範囲を外れているため、鉄損Ｗ15/50
が高くなっている。On the other hand, the steel sheets No. 9 and No. 21
Is out of the range of the present invention, so that the iron loss W 15/50 is high. In addition, the steel sheets No. 15 and No. 22 have a core loss W 15/50 because the winding temperature during hot rolling is out of the range of the present invention.
Is high.
【００２９】No.11の鋼板は、Ｃが本発明の範囲を超え
ているので、鉄損Ｗ15/50が高いばかりでなく、磁気時
効の問題がある。No.12の鋼板は、Mnが本発明の範囲を
超えているので、鉄損Ｗ15/50は低いものの、磁束密度
Ｂ50が低くなっている。No.13の鋼板は、Alが本発明の
範囲を下回っているので鉄損Ｗ15/50が高くなってい
る。N0.14の鋼板は、Ｎが本発明の範囲を超えているの
で、鉄損Ｗ15/50が高くなっている。The steel sheet No. 11 has not only a high iron loss W 15/50 but also a problem of magnetic aging since C exceeds the range of the present invention. In the steel sheet No. 12, since the Mn is beyond the range of the present invention, the iron loss W15 / 50 is low, but the magnetic flux density B50 is low. No. 13 steel sheet has a high iron loss W 15/50 because Al is below the range of the present invention. The N0.14 steel sheet has a high iron loss W 15/50 because N exceeds the range of the present invention.
【００３０】No.16とNo.23の鋼板は、Ｐ、Sn、Sb、の何
れもが本発明の範囲を外れているので、鉄損Ｗ15/50が
高くなっている。No.24の鋼板は、Siの範囲が本発明の
範囲より高いので、鉄損Ｗ15/50は低く押さえられてい
るものの、磁束密度Ｂ50が低くなっている。No.10の鋼
板は、Ｐが高すぎたため、冷間圧延時に破断して製品と
ならなかった。The steel sheets No. 16 and No. 23 have a high iron loss W 15/50 because all of P, Sn and Sb are out of the range of the present invention. In the steel sheet No. 24, since the range of Si is higher than the range of the present invention, the iron loss W 15/50 is kept low, but the magnetic flux density B 50 is low. The steel sheet No. 10 broke during cold rolling and did not become a product because P was too high.
【００３１】[0031]
【表１】 [Table 1]
【００３２】[0032]
【発明の効果】以上説明したように、本発明において
は、Ｓ＝10ppm以下の極低Ｓ材において、Ｐを0.03〜0.1
5％、あるいはSb＋1/2Snを0.001〜0.05％の範囲で含有
させ、かつ、熱延時の巻取温度を制御しているので、無
方向性電磁鋼板の鉄損を大幅に低下させることができ
る。さらに、Sb＋1/2Snの範囲を0.001〜0.005％に限定
することにより、より低い鉄損を得ることができる。As described above, according to the present invention, in an extremely low S material of S = 10 ppm or less, P is set to 0.03 to 0.1.
Since 5% or Sb + 1 / 2Sn is contained in the range of 0.001 to 0.05% and the winding temperature during hot rolling is controlled, the iron loss of the non-oriented electrical steel sheet can be significantly reduced. Further, by limiting the range of Sb + 1 / 2Sn to 0.001 to 0.005%, lower iron loss can be obtained.
【００３３】本発明に係る無方向性電磁鋼板は、鉄損が
低いことを要求される電気材料として、トランスの鉄
心、モータのコア等、広く種々の用途に使用する事がで
きる。The non-oriented electrical steel sheet according to the present invention can be used for a wide variety of applications, such as a transformer core and a motor core, as an electrical material required to have low iron loss.
【図面の簡単な説明】[Brief description of the drawings]
【図１】Ｓ量と磁気特性（鉄損）との関係を示す図であ
る。FIG. 1 is a diagram showing the relationship between the amount of S and magnetic properties (iron loss).
【図２】熱延時の巻取温度と磁気特性（鉄損）との関係
を示す図である。FIG. 2 is a diagram showing a relationship between a winding temperature during hot rolling and magnetic characteristics (iron loss).
Claims (3)
3.5％、Mn：0.05〜1.0％、Ｎ：0.005％以下（０を含
む）、Al：0.1 〜1.0％、Ｓ：0.001％以下（０を含
む）、Ｐ：0.03〜0.15％を含み、残部が実質的にFeから
なるスラブを巻取温度750℃以下で熱間圧延し、引き続
き熱延板焼鈍を行ない、酸洗後、一回の冷間圧延、もし
くは中間焼鈍をはさんだ二回以上の冷間圧延により、所
定の板厚とし、仕上焼鈍を実施することを特徴とする鉄
損の低い無方向性電磁鋼板の製造方法。(1) C: 0.005% or less by weight, Si: 1.5 to
3.5%, Mn: 0.05 to 1.0%, N: 0.005% or less (including 0), Al: 0.1 to 1.0%, S: 0.001% or less (including 0), P: 0.03 to 0.15%, the balance being A slab substantially made of Fe is hot-rolled at a winding temperature of 750 ° C. or lower, and subsequently hot-rolled sheet annealing is performed, and after pickling, one cold rolling or two or more cold-rolling steps including intermediate annealing are performed. A method for producing a non-oriented electrical steel sheet having a low iron loss, wherein a predetermined thickness is obtained by cold rolling and finish annealing is performed.
〜3.5％、Mn：0.05〜1.0％、Ｎ：0.005％以下（０を含
む）、Al：0.1 〜1.0％、Ｓ：0.001％以下（０を含
む）、Ｐ：0.15％以下（０を含む）、Sb＋1/2Sn：0.001
〜0.05％を含み、残部が実質的にFeからなるスラブを巻
取温度750℃以下で熱間圧延し、引き続き熱延板焼鈍を
行ない、酸洗後、一回の冷間圧延、もしくは中間焼鈍を
はさんだ二回以上の冷間圧延により、所定の板厚とし、
仕上焼鈍を実施することを特徴とする鉄損の低い無方向
性電磁鋼板の製造方法。2. C: 0.005% or less, Si: 1.5% by weight
3.5%, Mn: 0.05-1.0%, N: 0.005% or less (including 0), Al: 0.1-1.0%, S: 0.001% or less (including 0), P: 0.15% or less (including 0) , Sb + 1 / 2Sn: 0.001
A slab containing approximately 0.05%, with the balance being substantially Fe, is hot-rolled at a winding temperature of 750 ° C. or lower, and subsequently hot-rolled sheet annealing is performed. After pickling, one cold rolling or intermediate annealing is performed. By cold rolling two or more times sandwiching
A method for producing a non-oriented electrical steel sheet having a low iron loss, wherein a finish annealing is performed.
造される鉄損の低い無方向性電磁鋼板。3. A non-oriented electrical steel sheet having a low iron loss produced by the method according to claim 1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10134233A JPH11315327A (en) | 1998-04-30 | 1998-04-30 | Manufacture of non-oriented silicon steel sheet with low iron loss, and non-oriented silicon steel sheet with low iron loss |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10134233A JPH11315327A (en) | 1998-04-30 | 1998-04-30 | Manufacture of non-oriented silicon steel sheet with low iron loss, and non-oriented silicon steel sheet with low iron loss |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH11315327A true JPH11315327A (en) | 1999-11-16 |
Family
ID=15123548
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10134233A Pending JPH11315327A (en) | 1998-04-30 | 1998-04-30 | Manufacture of non-oriented silicon steel sheet with low iron loss, and non-oriented silicon steel sheet with low iron loss |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH11315327A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009518546A (en) * | 2005-12-27 | 2009-05-07 | ポスコ カンパニーリミテッド | Non-oriented electrical steel sheet excellent in magnetism and method for producing the same |
| CN102671940A (en) * | 2012-05-23 | 2012-09-19 | 山西太钢不锈钢股份有限公司 | Rolling method for producing phase changes in finish rolling process of low-grade non-oriented silicon steel |
-
1998
- 1998-04-30 JP JP10134233A patent/JPH11315327A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009518546A (en) * | 2005-12-27 | 2009-05-07 | ポスコ カンパニーリミテッド | Non-oriented electrical steel sheet excellent in magnetism and method for producing the same |
| CN102671940A (en) * | 2012-05-23 | 2012-09-19 | 山西太钢不锈钢股份有限公司 | Rolling method for producing phase changes in finish rolling process of low-grade non-oriented silicon steel |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR100658408B1 (en) | An electromagnetic steel sheet having superior formability and magnetic properties and a process for the production of the same | |
| KR940008933B1 (en) | Method of producing non-oriented electromagnetic steel strip having superior magnetic properties and appearance | |
| JP2000129410A (en) | Nonoriented silicon steel sheet high in magnetic flux density | |
| JP2000256751A (en) | Production of non-oriented silicon steel sheet low in core loss | |
| JP2000017330A (en) | Production of nonoriented silicon steel sheet low in iron loss | |
| JP2888226B2 (en) | Non-oriented electrical steel sheet with low iron loss | |
| JPH11315327A (en) | Manufacture of non-oriented silicon steel sheet with low iron loss, and non-oriented silicon steel sheet with low iron loss | |
| JP3952762B2 (en) | Non-oriented electrical steel sheet with excellent iron loss and caulking properties | |
| JPH11131196A (en) | Nonoriented silicon steel sheet minimal in iron loss | |
| JP4062833B2 (en) | Method for producing non-oriented electrical steel sheet with excellent magnetic properties | |
| JPH11302741A (en) | Production of nonoriented silicon steel sheet low in core loss and nonoriented silicon steel sheet low in core loss | |
| JPH06256847A (en) | Manufacture of grain-oriented electrical steel sheet having excellent magnetic characteristic | |
| JPH11124626A (en) | Production of nonoriented silicon steel sheet reduced in iron loss | |
| JP3766745B2 (en) | Non-oriented electrical steel sheet with low iron loss after magnetic annealing | |
| JP3424178B2 (en) | Non-oriented electrical steel sheet with low iron loss | |
| JPH1046245A (en) | Manufacture of nonoriented magnetic steel sheet reduced in iron loss after magnetic annealing | |
| JPH1112701A (en) | Nonoriented silicon steel sheet with low iron loss | |
| JPH11315326A (en) | Manufacture of nonoriented silicon steel sheet with low iron loss, and nonoriented silicon steel sheet with low iron loss | |
| JP2712913B2 (en) | Grain-oriented electrical steel sheet and its manufacturing method | |
| JPH1171650A (en) | Nonoriented silicon steel sheet low in core loss | |
| JPH11189824A (en) | Production of nonoriented silicon steel sheet with low iron loss | |
| JPH1161260A (en) | Manufacture of nonoriented silicon steel sheet with low iron loss | |
| JPH11158589A (en) | Nonoriented silicon steel sheet excellent in magnetic property after stress relieving annealing and its production | |
| JPH1112700A (en) | Non-oriented electrical sheet having low iron loss | |
| JPH1088297A (en) | Nonoriented silicon steel sheet reduced in iron loss after magnetic annealing |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20050218 |
|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20050617 |